EP3235923B1 - Hochfester flachstahl mit dehngrenze von 800 mpa und mehr und herstellungsverfahren dafür - Google Patents

Hochfester flachstahl mit dehngrenze von 800 mpa und mehr und herstellungsverfahren dafür Download PDF

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EP3235923B1
EP3235923B1 EP15869228.5A EP15869228A EP3235923B1 EP 3235923 B1 EP3235923 B1 EP 3235923B1 EP 15869228 A EP15869228 A EP 15869228A EP 3235923 B1 EP3235923 B1 EP 3235923B1
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temperature
strength
rolling
steel
steel plate
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French (fr)
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EP3235923A1 (de
EP3235923A4 (de
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Gang Liu
Ana YANG
Zigang LI
Fengming SONG
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
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    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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Definitions

  • the disclosure relates to a high-strength steel with a yield strength at a level of 800 MPa and a production method thereof.
  • the strength of the steel for engineering machinery is increased continuously from 500-600 MPa to 700 MPa, 800 MPa, and even 1000 MPa or higher in a short period of time.
  • the harsh use environment and load conditions of the ultrahigh-strength steel for engineering machinery impose rigid requirements on the quality of the steel material, including strength, impact resistance, bending property, weldability, strip shape, etc.
  • Chinese Patent Application No. 201210209649.5 discloses a method for producing a high-strength steel plate with a tensile strength at a level of 800MPa, wherein no Ni element is added, and a process of on-line quenching + tempering (DQ+T) is utilized to obtain a structure of tempered martensite + tempered lower bainite, wherein the yield strength is only 700MPa.
  • DQ+T on-line quenching + tempering
  • 2011100343384.3 discloses a high-strength steel with a strength at a level of 750-880 MPa for vehicles and a production method thereof, wherein a TMCP process is utilized to produce a hot-rolled high-strength steel coil which is coiled at 560-600 °C.
  • EP 1 712 651 A1 discloses A high-strength seamless steel pipe for oil wells excellent in sulfide stress cracking resistance.
  • the steel pipe comprises, on the percent by mass basis, C: 0.1 to 0.20 %, Si: 0.05 to 1.0 %, Mn: 0.05 to 1.0 %, Cr: 0.05 to 1.5 %, Mo: 0.05 to 1.0 %, Al: 0.10 % or less, Ti: 0.002 to 0.05 % and B: 0.0003 to 0.005 %, with a value of equation "C + (Mn/6) + (Cr/5) + (Mo/3)" of 0.43 or more, with the balance being Fe and impurities, and in the impurities P: 0.025 % or less, S: 0.010 % or less and N: 0.007 % or less.
  • JP 2012-077336 A discloses a hot rolled steel sheet which contains, by mass: C: 0.08-0.25%, Si: 0.01-1.0%, Mn: 0.8-1.5%, P, S, A1 adjusted to an appropriate range, Nb: 0.001-0.05%, Ti: 0.001-0.05%, Mo: 0.1-1.0%, Cr: 0.1-1.0%, B: 0.0005-0.0050%, remainder Fe and unavoidable impurities.
  • the steel sheet has, as main phase, a tempered-martensite phase.
  • the average particle diameter of the prior-austenite grain in the cross section parallel to a rolling direction is 20 micrometers or less and that orthogonal to the rolling direction is 15 micrometers or less.
  • EP 0 861 915 A1 discloses a high-tensile-strength steel having excellent arrestability and a tensile strength of not less than 900 MPa, as well as a method of manufacturing the same.
  • the steel has the composition (% by weight): C: 0.02% to 0.1%. Si: not greater than 0.6%; Mn: 0.2% to 2.5% Ni: greater than 1.2% but not greater than 2.5%; Nb 0.01% to 0.1%. Ti 0.005% to 0.03%, N 0.001% to 0.006%: Al: not greater than 0.1%: and optional elements.
  • Ceq of the B-free steel is 0.53-0.7% and Ceq of the B-bearing steel is 0.4-0.58%
  • the micro structure of the steel may be a mixed structure of martensite (M) and lower bainite (LB) occupying at least 90 vol.% in the microstructure.
  • LB occupying at least 2.vol% in the mixed structure, and the aspect ratio of prior austenite grains is not less than 3.
  • An object of the disclosure is to provide a high-strength steel having a yield strength at a level of 800MPa and a method of producing the same, wherein an on-line quenching + tempering process is utilized, and the high-strength steel has a yield strength of 800-950 MPa, a tensile strength of 850-1000 MPa, an elongation > 12 %, and an impact energy at-40 °C > 40 J.
  • the high-strength steel plate has a yield strength of 800-950MPa, a tensile strength of 850-1000MPa, an elongation >12 %, and an impact energy at -40 °C >40 J.
  • the microstructure of the high-strength steel plate is tempered martensite.
  • C Carbon has the effect of solid solution strengthening. It regulates the strength and plastic toughness of the martensitic structure.
  • the on-line quenched tensile strength of low-carbon martensite and the carbon content have the following relationship:
  • the control of 0.7% ⁇ Mo+0.8Ni+0.4Cr+6V ⁇ 1.1% is mainly used to guarantee equal-strength matching welding of the 800 MPa high-strength steel, and adjust the strength and low-temperature toughness of the welding heat affected zone to realize the optimal matching with the parent steel plate in terms of strength and low-temperature toughness.
  • Mo, Ni and Cr elements all can decrease the critical cooling speed of the steel, increase the hardenability of the steel, and increase the strength of the welded joints.
  • Mo reacts with C to form compounds at high temperatures, and it has the effect of resisting softening of the welded joints.
  • Mo and Ni elements both have the effect of refining structures and improving toughness.
  • V and N react to form nano-scale V(C, N) particles which can resist softening of the joints.
  • the collaboration of Mo, Ni, Cr and V elements can regulate the strength and toughness of the welding heat affected zone based on the strength of the parent material.
  • the total amount of Mo, Ni, Cr and V according to the disclosure is required to meet 0.7% ⁇ Mo+0.8Ni+0.4Cr+6V ⁇ 1.1%. If lower than 0.7%, both the strength and low-temperature toughness of the welded joints will be low; if higher than 1.1%, the strength of the welded joints is rather high, and thus weld cracking tends to occur.
  • the control of 3.7 ⁇ Ti/N ⁇ 7.0 according to the disclosure can protect B atoms in the steel, so that B can be sufficiently solid-dissolved to increase the hardenability.
  • the control of 1.0 ⁇ Ca/S ⁇ 3.0 according to the disclosure can spheroidize sulfides in the steel, so as to improve the low-temperature toughness and weldability of the steel.
  • a method of producing a high-strength steel plate with a yield strength at a level of 800 MPa comprises the following steps:
  • a composition as described above is smelted in a converter or electrical furnace, subjected to refining, and cast to a cast blank;
  • the cast blank is heated at 1150-1270°C in a furnace, wherein, when the core of the cast blank arrives at the temperature, the temperature is held, and the holding time is >1.5h;
  • Tempering heat treatment The tempering temperature is 400-550°C; when the temperature of the core of the steel plate arrives at the furnace temperature, the temperature is held, and the holding time is 20-180min.
  • the beneficial effects of the disclosure include: By using a process of controlling rolling, controlling cooling, and on-line quenching + tempering, the disclosure makes control with respect to the chemical compositional design, the structure of the parent material, the quenching heating temperature, the tempering heating temperature and the like, so as to obtain good elongation, low-temperature toughness and other properties while guaranteeing ultrahigh strength.
  • the high-strength steel of Grade 800MPa produced using the composition and process of the disclosure possesses uniform tempered martensitic structure; the properties vary little for different thicknesses, or for the head, middle and tail of a steel coil (steel plate); and the low-temperature impact toughness also increases greatly.
  • a 50 kg vacuum electric furnace was used for smelting.
  • the compositions of the steel according to the disclosure are shown in Table 1.
  • Liquid steel smelted in the 50 kg vacuum electric furnace was cast into steel blanks having a thickness of 120mm.
  • the steel blanks were placed into an electric furnace for heating.
  • the steel blanks were rolled to a target thickness of 10 mm in multiple paths.
  • the final rolling temperature was 820-920°C.
  • the final rolling temperature Tf met: Ar 3 ⁇ Tf ⁇ Tnr.
  • the reduction rate at the final path was set to 17%.
  • On-line quenching was conducted after rolling, wherein the quenching cooling speed was V>e (5.3-2.53C-0.16Si-0.82Mn-0.95Cr-1.87Mo-160B) °C/s.
  • the final cooling temperature was (Ms ⁇ 150)°C or less.
  • the tempering temperature was 400-550°C, and the tempering time was 20-180 min after the core of the steel plate arrived at the tempering temperature.
  • the specific process conditions are shown in Table 2.
  • the on-line quenched + tempered steel plate was subjected to longitudinal tensile testing and longitudinal impact testing.
  • the properties of various sample plates are shown in Table 3.
  • Table 3 a quenched and tempered high-strength steel having a yield strength of 8000MPa or higher can be manufactured according to the disclosure, wherein the tensile strength is 850-1000 MPa, the elongation is >12%, and the impact energy at -40°C is >40J.
  • Figs. 1-3 show the metallographical structure images of the test steels of Examples 1, 5 and 8. As can be seen, the metallographical structures of the final steel plates are homogeneous lath-shaped tempered martensite, and the structures are fine. Table 1: Chemical compositions of the Examples according to the disclosure Unit: weight percentage No.

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  • Engineering & Computer Science (AREA)
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  • Heat Treatment Of Steel (AREA)

Claims (2)

  1. Hochfeste Stahlplatte, die eine Streckgrenze von 800-950 MPa, eine Zugfestigkeit von 850-1000 MPa, eine Dehnungsfähigkeit von >12% und eine Aufprallenergie bei -40°C von >40J aufweist, und die in Gewichtsprozent aus den folgenden Bestandteilen besteht: C: 0,06-0,14%, Si: 0,10-0,30%, Mn: 0,80-1,60%, Cr: 0,20-0,70%, Mo: 0,10-0,40%, Ni: 0-0,30%, Nb: 0,010-0,030%, Ti: 0,010-0,030%, V: 0,010-0,050%, B: 0,0005-0,0030%, Al: 0,02-0,06%, Ca: 0,001-0,004%, N: 0,002-0,005%, P≤0,020%, S≤0,010%, O≤0,008%, und der Rest aus Fe und unvermeidlichen Unreinheiten; wobei die obigen Elemente dem folgenden Verhältnis entsprechen:
    0,40%<Ceq<0,50%, Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/15,
    0,7%≤Mo+0,8Ni+0,4Cr+6V≤1,1%; 3,7≤Ti/N≤7,0; und 1,0≤Ca/S≤3,0;
    wobei die hochfeste Stahlplatte eine Mikrostruktur aus angelassenem Martensit aufweist.
  2. Verfahren zum Herstellen der hochfesten Stahlplatte nach Anspruch 1, aufweisend die folgenden Schritte:
    1) Schmelzen und Gießen
    Schmelzen einer Zusammensetzung wie in Anspruch 1 beschrieben in einem Konverter oder elektrischen Ofen, Raffinieren und Gießen zu einem Gussrohling;
    2) Brammenerwärmung
    Erwärmen des Gussrohlings in einem Ofen bei 1150-1270°C, wobei, wenn die Temperatur des Kerns des Gussrohlings die Temperatur des Ofens erreicht, die Temperatur gehalten wird, und die Haltezeit > 1,5 h beträgt;
    3) Walzen
    Walzen des Gussrohlings bis zu einer Solldicke durch Einzelgerüst-Pilgerwalzen oder kontinuierliches Mehrgerüst-Warmwalzen, wobei eine Endwalztemperatur 820-920°C beträgt und wobei die Endwalztemperatur Tf die Gleichung: Ar3<Tf<Tnr erfüllt, wobei Ar3 eine Temperatur ist, bei der hypo-eutektoider Stahlaustenit anfängt, zu Ferrit zu konvertieren:
    Ar3=901-325C-92Mn-126Cr-67Ni-149Mo; wobei Tnr eine kritische Nichtrekristallisationstemperatur ist:
    Tnr=887+464C+(6445Nb-644sqrt(Nb))+(732V-230sqrt(V))+890Ti+363Al-357Si;
    wobei eine Walzverringerungsrate auf einem Endwalzpfad >15% beträgt;
    4) Abschreckungswärmebehandlungsvorgang
    Durchführen von Abschrecken auf dem Band auf (Ms-150) °C oder niedriger nach dem Walzen durch Verwendung eines Laminarkühlungssystems, um eine Kühlungsgeschwindigkeit V>e(5,3-2,53c-0,16Si-0,82Mn-0,95Cr-1,87Mo-160B)°C/s zu steuern, um die Bildung einer vollmartensitischen Struktur sicherzustellen, wobei Ms eine Temperatur ist, bei der die Transformation von Martensit beginnt,

            Ms=539-423C-30,4Mn-17,7Ni-12,1Cr-11,0Si-7,0Mo;

    5) Glühwärmebehandlungsvorgang
    Durchführen einer Glühwärmebehandlung bei einer Glühtemperatur von 400-550°C; wobei, wenn die Temperatur des Kerns der Stahlplatte die Temperatur des Ofens erreicht, die Temperatur gehalten wird, und die Haltezeit 20-180 min beträgt.
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